Fluorosulphates useful as electrode materials

ABSTRACT

A material is made up of particles of an optionally-doped fluorosulphate. The fluorosulphate has a distorted Tavorite type structure of formula (A 1−a A′ a )x(Z 1−b Z′ b )z(SO 4 ) s F f  (I) where A=Li or Na, A′ 0 a hole or at least one doping element, Z=at least one element selected from Fe, Co and Ni, Z′=a hole or at least one doping element, the indices a, b, x, z, s, and f are selected to assure the electroneutrality of the compound and a≧0, b≧0, x≧0, z&gt;0, s&gt;0, f&gt;0, the respective quantities a and b of dopant A and Z′ being such that the Tavorite type structure is preserved. The material is obtained from the precursors thereof by an ionothermal route or ceramic route in a closed reactor. The material is of particular use as an active electrode material.

The present invention relates to a fluorinated material that can be used as an electrode active material, and also to a process for the production thereof.

PRIOR ART

Lithium batteries are known which use an insertion compound as a basis for the operation of the positive electrode, such as Li_(x)CoO₂, 0.4≦x≦1 which is used pure or in solid solution with nickel and manganese and aluminum. The main obstacles to the generalization of this type of electrochemistry are the rarity of cobalt and the excessively positive potential of the transition oxides, with, as consequences, safety problems for the battery.

Li_(x)T^(M) _(m)Z_(y)P_(1−s)O₄ compounds (“oxyanions”) are also known in which T^(M) is chosen from Fe, M and Co, and Z represents one or more elements that have a valence between 1 and 5 and that may be substituted into the sites of the transition metals or of the lithium. These compounds exchange only the lithium and have only a very low electronic and ionic conductivity. These handicaps may be overcome by the use of very fine particles (such as nanoparticles and by the deposition of a carbon coating by pyrolysis of organic compounds. The drawbacks associated with the use of nanoparticles are a low tap density which results in a loss of specific energy, and this problem is further aggravated by the deposition of carbon. Furthermore, the deposition of carbon takes place at high temperature, under reducing conditions. In practice, it is difficult to use transition elements other than Fe^(II) and Mn^(II), the elements Co^(II) and Ni^(II) being readily reduced to the metallic state. The same applies for Fe^(III), Mn^(III), Cr^(III), V^(III) and V^(IV) which are advantageous dopants for increasing the ionic or electronic conductivity.

Other compounds have been proposed, especially compounds corresponding to the general formula A_(a)M_(b)(SO₄)_(c)Z_(d) in which A represents at least one alkali metal. Z represents at least one element chosen from F and OH, and M represents at least one divalent or trivalent metal cation. L. Sebastian et al., [J. Mater. Chem. 2002, 374-377] describe the preparation of LiMgSO₄F via a ceramic route, and also the crystallographic structure of said compound which is isotypic of the structure of tavorite LiFeOHPO₄. The authors mention the high ionic conduction of this compound, and suggest that the compounds LiMSO₄F in which M is Fe, Co or Ni, which would be isostructural, appear to be significant for the redox insertion/extraction of lithium involving M^(II)/M^(III) oxidation states. The authors also specify that the preparation of the compounds of Fe, Ni or Co via a ceramic route is in progress, but no subsequent publication regarding these compounds has been made.

Moreover, US-2005/0163699 describes the preparation, via a ceramic route, of the aforementioned compounds A_(a)M_(b)(SO₄)_(c)Z_(d). The technique is illustrated by concrete examples regarding compounds in which M is Ni, Fe, Co, Mn, (MnMg), (FeZn), or (FeCo). These compounds are prepared, via a ceramic route, from LiF, precursor of Li, and from the sulfate of the M element or elements. Among these compounds, the most advantageous are the compounds that contain Fe, since besides their relatively low cost, they are capable, on the basis of structural and chemical considerations (especially the ionocovalence of the bonds), of exhibiting advantageous electrochemical properties over a range of potential that is desirable for guaranteeing a reliable use for large-volume applications. For reasons of inductive effect, the sulfates should have higher potentials from the phosphates, regardless of their structure. Examples for preparing compounds containing various metallic elements are described, but no electrochemical property is reported. Thus, example 2 describes the preparation of an LiFeSO₄F compound via a ceramic method at 600° C. which wives a non-homogenous compound, then 500° C. where the compound is red/black, or else at 400° C. in air where the compound is red. This method is capable of enabling the reduction of the SO₄ ²⁻ group by Fe²⁺ in the absence of oxygen according to: SO₄ ²⁻+Fe²⁺

SO₂+2O²⁻2Fe³⁺. The red color observed in the compounds obtained at the various temperatures is due to the O²⁺/Fe³⁺ association in a crystal lattice such as the oxide Fe₂O₃. It is furthermore known that the compounds of Fe^(II) oxidize in air from 200° C. giving Fe^(III), and the preparation from example 2 at 400° C. in air confirms it. The compounds containing iron that are prepared via a ceramic route starting from LiF and iron sulfate according to US-2005/0163699 do not therefore consist of LiFeSO₄F. Similarly, it appears that the compounds in which M is Co, Ni are not stable at the temperatures used during the recommended preparation via a ceramic route. It is not therefore plausible that the compounds described in US-2005/0163699 have actually been obtained.

INVENTION

The objective of the present invention is to provide a novel electrode material having an improved electrochemical activity close to the theoretical capacity (that is to say a material capable of inserting one alkali metal ion per fluorinated oxyanion unit), and also a process that makes it possible to produce said material in a reliable, rapid and economical manner.

The material of the present invention consists of particles of a fluorosulfate which has a distorted tavorite-type structure and which corresponds to the following formula (I):

(A_(1−a)A′_(a))_(x)(Z_(1−b)Z′_(b))_(z)(SO₄)_(s)F_(f)  (I)

in which:

-   -   A represents Li or Na;     -   A′ represents a vacancy or at least one dopant element;     -   Z represents at least one element chosen from Fe, Co and Ni;     -   Z′ represents a vacancy or at least one dopant element;     -   the indices a, b, x, z, s, and f are chosen so as to ensure the         electroneutrality of the compound, and a≧0, b≧0, x≧0, z>0, s>0,         f>0;     -   the respective amounts a and b of dopant A and Z′ are such that         the tavorite-type structure is preserved.

The tavorite structure comprises ZO₄F₂ octahedra centered about Z connected by apical fluorines forming chains along the c axis. The octahedra all have F atoms in the trans position, but they are divided into two different types. The chains are connected together via isolated. SO₄ tetrahedra, thus creating a three-dimensional structure and defining tunnels along the [100], [010] and [101] axis, the A_(1−a)A′_(a) element of a compound (I) lodging in said tunnels (3D diffusion).

When A is Li, the distorted tavorite-type structure of compound (I) has a triclinic lattice of space group P−1. When A is Na, the distorted tavorite-type structure of compound (I) has a monoclinic lattice (P2₁/C).

FIGS. 1 and 2 are schematic representations respectively of the distorted tavorite-type structure having a triclinic lattice and having a monoclinic lattice.

FIG. 3 is a comparative view of the triclinic lattice on the left and the monoclinic lattice on the right.

FIG. 4 represents the image obtained by SEM for the LiFeSO₄F material from example 1.

FIG. 5 a represents the TEM image, more particularly the corresponding SAED diagram, for the LiFeSO₄F material from example 1 and FIG. 5 b represents the EDS spectrum which shows the presence of F. The intensity is given on the y-axis (in arbitrary units) as a function of the energy F (in keV) on the x-axis.

FIG. 6 represents the X-ray diffraction diagram and, in the form of an insert, the structure of the LiFeSO₄F material from example 1.

FIG. 7 represents the diagram obtained during the characterization by TGA coupled with a mass spectrometry of the LiFeSO₄F material from example 1.

FIG. 8 represents the change in the X-ray diffraction diagram during the increase in the temperature, for a sample of LiFeSO₄F.

FIG. 9 represents the X-ray diffraction diagram for the FeSO₄+LiF mixture FIG. 9 a) and for the material obtained after the heat treatment (FIG. 9 b).

FIGS. 10, 11, 12 and 13 represent the X-ray diffraction diagram of the LiFeSO₄F material obtained respectively in examples 2, 3, 4 and 5.

FIGS. 14 and 15 represent the X-ray diffraction diagram and the diagram obtained during the characterization by TGA of the LiCoSO₄F material from example 6.

FIG. 16 represents the change in the X-ray diffraction diagram during the increase in the temperature, for a sample of LiCoSO₄F.

FIGS. 17 and 18 respectively represent the X-ray diffraction diagram and the diagram obtained during the characterization by TGA of the LiNiSO₄F material from example 7.

FIG. 19 represents the change in the X-ray diffraction diagram during the increase in the temperature, for a sample of LiNiSO₄F.

FIGS. 20 and 21 represent the X-ray diffraction diagram respectively of the material Fe_(0.5)Mn_(0.5)SO₄.H₂O from example 8 and of the material NaFeSO₄F from example 9.

FIGS. 22 and 23 represent the X-ray diffraction diagram of the LiFeSO₄F material obtained respectively in examples 10 and 11.

FIG. 24 represents, on the left, the X-ray diffraction diagram of the LiFeSO₄F material obtained, in example 12 and, on the right, an SEM micrograph of said material.

FIGS. 25, 26 and 27 represent the X-ray diffraction diagram respectively of the NaFeSO₄F material from example 13, of the NaCoSO₄F material from example 14 and of the FeSO₄F material from example 15.

FIGS. 28 a, b and c relate to several samples of LiFeSO₄F prepared according to example 3. FIG. 28 a represents the variation in the potential (in V) as a function of the insertion rate x of lithium and (in the form of an insert) the variation in the capacity C (in mAh/g) as a function of the number of cycles N at a C/10 regime. FIG. 28 b represents the variation in the potential (in V) as a function of the insertion rate x of lithium at a C/2 regime. FIG. 28 c represents the variation in the capacity as a function of the regime R.

FIG. 29 represents the variation in the potential P (in V) as a function of the insertion rate x of lithium (left-hand curve) and the variation of the capacity C (in mAh/g) as a function of the number of cycles N (right-hand curve) for the LiFeSO₄ material from example 12.

FIG. 30 represents the variation in the potential P (in V) as a function of the insertion rate x of lithium for the NaFeSO₄F material from example 13.

In all the X-ray diffraction diagrams, the intensity I (in arbitrary units) is given on the y-axis, and the wavelength 2θ is given on the x-axis.

In the TGA diagrams, % TG indicates the weight loss as a function of the temperature T (in ° C.) and optionally DSC indicates the amount of energy in (mW).

A compound according to the invention is in the form of grains, the dimension of which is less than 100 μm, or even less than 1.00 nm.

When A′ is a dopant element, A′ may be an alkali metal different from A, an alkaline-earth metal or a 3d metal, in particular Ti, V, Cr, Mn, Fe, Mn, Co or Cu. Generally, the “a” content of dopant A′ is preferably less than 0.25%, that is to say a<0.25.

When Z′ is a dopant element, Z′ may be a metal chosen from alkali metals, Mn, Mg, Co, Sc, Ti, V, Cr, Zn, Al, Ga, Zr, Nb and Ta in at least one of their degrees of oxidation. Generally, the “b” content of dopant Z′ is preferably less than 25%, that is to say b<0.25. Particularly advantageous Z′ dopants are Mn, Mg, Zn, Ti and Al.

Compounds according to the invention that are particularly preferred are those which correspond to the formulae Li(Z_(1−b)Z′_(b))SO₄F and Na(Z_(1−b)Z′_(b))_(z)SO₄F, in particular LiFeSO₄F, LiCoSO₄F, LiNiSO₄F, and their solid solutions, NaFeSO₄F, NaCoSO₄F, NaNiSO₄F and their solid solutions, and also the solid solutions Li(Z_(1−b)Mn_(b))SO₄F and Na(Z_(1−b)Z′_(b))SO₄F in which Z is Fe, Co or Ni, b≦0.2.

One particular category of compounds (I) comprises the compounds in which the (Z_(1−b)Z′_(b)) group represents more than one element. These are compounds in which Z represents more than one element chosen from Fe, Co and Ni, and also compounds in which b≠0, the two cases possibly being combined.

A compound (I) in which x=0, that is to say a compound of formula (Z_(1−b)Z′_(b))_(z)(SO₄)_(s)F_(f), in particular a compound ZSO₄F, more particularly FeSO₄F is advantageous because it makes it possible to construct primary electrochemical generators in the charged state with a lithium anode and a liquid or gel type electrolyte, or secondary generators, in particular with polymer electrolytes.

A material (I) according to the invention in which x>0 may be obtained from precursors of the elements which form it, via a ceramic route or via an ionothermal route.

The precursor of A or of A′ may be chosen from inorganic acid salts (such as carbonates and hydrogen carbonates, hydroxides, peroxides and nitrates), volatile organic acid salts (such as acetates and formates), heat-decomposable acid salts (such as oxalates, malonates and citrates), fluorides and sulfates. Among such precursors, Li₂CO₃, LiHCO₃, LiOH, Li₂O, Li₂O₂, LiNO₃, LiCH₃CO₂, LiCHO₂, Li₂C₂O₄, Li₃C₆H₅O₇, Na₂CO₃, NaOH, Na₂O₂, NaNO₃, NaCH₃CO₂, NaCHO₂, Na₂C₂O₄, Na₃C₆H₅O₇, and hydrates thereof are preferred in particular. The precursors of Li or Na that provide at least two constituents of the final product such as fluorides and sulfates are particularly preferred, especially LiF, NaF, LiHSO₄ and the sulfates Li₂SO₄, Na₂SO₄ and NaHSO₄ in hydrated form.

The precursor of a Z or Z′ element is preferably chosen from the sulfates of Z or of Z′ that have a tavorite-type structure and that will make it possible to obtain the tavorite-type structure of compound (I).

When the precursors of A, of A′, of Z or of Z′ do not provide any F or S elements, or provide an insufficient amount with respect to the stoichiometry of compound (I) to be prepared, it is possible to add precursors providing solely one or several F or S elements.

The precursors of the oxyanion SO₄ ²⁻ may be chosen from the acid H₂SO₄, and its thermolabile ammonium, amine, imidazole or pyridine salts such as, for example, NH₄HSO₄, (NH₄)₂SO₄, (C₃H₅)HSO₄, (C₅H₆)₂SO₄ and (C₃H₅)₂SO₄, (C₅H₆)HSO₄.

The precursors of S may also be chosen from the salts of Mg or Ca. By way of example, mention may be made of the compounds A″(HSO₄)₂, and A″SO₄, A″HPO₄, and A″₂P₂O₇, A″(PO₃)₂ in which A″ represents an alkaline-earth metal (Mg, Ca).

The fluoride ion precursors may be chosen from ammonium fluorides (NH₄F.nHF), imidazolium fluorides (C₃H₅N₂F.nHF) or pyridinium fluorides (C₅H₆NF.nHF) 0≦n≦5. Of course, it is possible to use several precursors for the same element.

In one particularly preferred embodiment, the precursor of Z and, where appropriate, the precursor of Z′ are chosen from the sulfates of the Z and/or Z elements. The precursor of A and, where appropriate, the precursor of A′ are chosen from the fluorides of the A an/or A′ elements. Preferably, use is made of sulfates in hydrate form, in particular in monohydrate form. It has been observed that, surprisingly, the use of a sulfate monohydrate precursor that has a distorted tavorite-type structure makes it possible to retain the more or less distorted tavorite-type structure during the reaction with the fluoride.

The reaction is topotactic due to the structural relationship between ZSO₄.H₂O and the corresponding Li and Na phases, based on maintaining the general arrangement of the SO₄ tetrahedra and ZO₄F₂ octahedra in the structural framework.

The monohydrate ZSO₄.H₂O may be obtained from ZSO₄.7H₂O either by heating under vacuum at a temperature between 150° C. and 450° C. (for example 200° C.), or by heating in an ionic liquid (for example 2 hours at 270° C. in EMI-TFSI).

The compounds (I) in which the (Z_(1−b)Z′_(b)) group represents more than one element are preferably prepared by using, as a precursor of Z and Z′, a solid solution of sulfate, preferably in hydrate form.

In one particular embodiment, a process that aims to prepare an Fe_(1−b)Z′_(b)SO₄.H₂O precursor comprises the following steps:

-   -   dissolving 1-b moles of FeSO₄.nH₂O and b moles of Z′SO₄.nH₂O in         water previously degassed by argon or nitrogen to avoid the         oxidation of Fe(II), b≦0.25 and n≦7;     -   adding an alcohol (for example ethanol or isopropanol) to give         rise to the precipitation of Fe_(1−b)Z′_(b)SO₄.nH₂O;     -   recovering (for example by centrifuging) the powder which is         formed; and     -   washing with alcohol, then heating at a temperature between 150         and 250° C. (for example at 200° C.) under vacuum for 1 hour.

The preparation of a precursor in which Z represents Fe and Co or Fe and Ni may be carried out in the same manner by choosing CoSO₄.nH₂O or NiSO₄.nH₂O for Z′SO₄.nH₂O, b then being less than 1.

A compound of the invention may be obtained by a synthesis process at temperatures of less than 330° C. via an ionothermal route.

The process via the ionothermal route comprises the following steps:

-   i) dispersing said precursors in a support liquid comprising at     least one ionic liquid consisting of a cation and of an anion, the     electric charges of which are balanced, in order to obtain a     suspension of said precursors in said liquid; -   ii) heating said suspension to a temperature of 25 to 330° C.; -   iii) separating said ionic liquid and the inorganic oxide of     formula (I) resulting from the reaction between said precursors.

The sulfate monohydrate precursor may be prepared previously, or prepared in situ in the ionic liquid, during a preliminary step.

The expression “ionic liquid” is understood to mean a compound that contains only anions and cations, the charges of which are balanced, and which is liquid at the temperature of the reaction for formation of the compounds of the invention, either pure, or as a mixture with an additive.

The amount of precursors present within the ionic liquid during step i) is preferably from 0.01% to 85% by weight, and more preferably from 5 to 60% by weight.

The respective amounts of the various precursors depend on the stoichiometry of the compound (I) to be prepared. Their determination is within the scope of the person skilled in the art, since the reactions are stoichiometric. Preferably, an excess of fluoride, preferably of the order of 5 to 25%, is used.

According to one preferred embodiment of the invention, the cation of ionic liquid is chosen from the cations of the following formulae:

in which:

-   -   the R⁴-R⁷, R¹⁷, R²⁷, R²⁴, R²⁸, R²⁹, R³⁷, R³⁴, R³⁹, R⁴³ and R⁴⁶         to R⁵⁷ radicals, independently of one another, represent a         C₁-C₂₄ alkyl, C₁-C₂₄ arylalkyl or (C₁-C₂₄)alkylaryl radical;     -   the R⁸-R¹⁶ radicals have the meaning given for R⁴ or they each         represent a (C₁-C₂₀)alkylaryl radical or an NR⁶³R⁶⁴ group;     -   the R¹⁸ to R²², R²³, R²⁵, R²⁶, R³⁰ to R³³, R³⁵, R³⁶, R³⁸, R⁴⁰ to         R⁴², R⁴⁴ and R⁴⁵ radicals represent a hydrogen atom, a C₁-C₂₄         alkyl, an or C₁-C₂₄ oxaalkyl radical or a —[(CH)₂]_(n)Q radical         in which Q represents —OH, —CN, —C(═O)OR⁵⁸, —C(═O)NR⁵⁹R⁶⁰,         —NR⁶¹R⁶², —CH(OH)CH₂OH, or else a 1-imidazoyl, 3-imidazoyl or         4-imidazoyl radical, and 0≦n≦12; and     -   R⁵⁸ to R⁶⁴, independently of one another, represent a hydrogen         atom, a C₁-C₂₀ alkyl, aryl or C₁-C₂₀ oxaalkyl radical.

Very particularly preferred are the imidazolium cations in which R²³═H or CH₃, R²⁴═CH₃, R²⁵═R²⁶═H, and R²⁷═C₂H₅, C₃H₇, C₄H₉, C₅H₁₁, C₆H₁₃, C₈H₁₇, (CH₂)₃OH, (CH₂)₃CN, (CH₂)₄OH, or (CH₂)₄CN, and the imidazolium cations in which R²³═H or CH₃, R²⁴═C₄H₉, R²⁵═R²⁶═H, R²⁷═(CH₂)₂OH, (CH₂)₂CN, (CH₂)₃OH, (CH₂)₃CN, (CH₂)₄OH, (CH₂)₄CN, or CH₂CH(OH)CH₂OH.

The anion of an ionic liquid is preferably chosen from Cl, Br, I, RSO₃ ⁻, ROSO₃ ⁻, [RPO₂]⁻, [R(R′O)PO₂]⁻, [(RO)₂PO₂]⁻, BF₄ ⁻, R_(f)BF₃ ⁻, PF₆ ⁻, R_(f)PF₅ ⁻, (R_(f))₂PF₄ ⁻, (R_(f))₃PF₃ ⁻, R_(f)CO₂ ⁻, R_(f)SO₃ ⁻, [(R_(f)SO₂)₂N]⁻, [(R_(f)SO₂)₂CH]⁻, [(R_(f)SO₂)₂C(CN)]⁻, [R_(f)SO₂C(CN)₂]⁻, [(R_(f)SO₂)₃C]⁻, N(CN)₂ ⁻, C(CN)₃ ⁻, [(C₂O₄)₂B]⁻ in which:

-   -   R and R′, which are identical or different, each represent a         C₁-C₂₄ alkyl, aryl or (C₁-C₂₄)alkylaryl radical; and

R_(f) is a fluoro radical chosen from C_(n)F_(2n+1) in which 0≦n≦8, CF₃OCF₂, HCF₂CF₂ and C₆F₅.

When the cation of the ionic liquid is an imidazolium cation, it is desirable for the C2 carbon of the imidazolium cation to be protected by an alkyl group, preferably having 1 to 4 carbon atoms, due to the fact that the precursor of the A element is a fluoride. Otherwise, the acid proton borne by the C2 carbon would give rise to the decomposition of the cation of the ionic liquid.

An ionic liquid having a high hydrophobic character favors the reaction between the precursor of A (AF) and the hydrated ZSO₄ precursor. It makes it possible to carry out the synthesis in an open reactor. A hydrophilic ionic liquid is less favorable, and it necessitates carrying out the synthesis in a sealed reactor under pressure.

1-Butyl-3-methylimidazolium trifluoromethanesulfonate (BMI-triflate), and 1-ethyl-3-methylimidazolium bis(trifluoromethanesulfonyl)imide (EMI-TFSI) are particularly preferred. EMI-TFSI, which is more hydrophobic than BMI-triflate, is particularly preferred.

According to one preferred embodiment of the invention, the temperature for heating the suspension during step ii) is between 100° C. and 330° C., and more preferably still between 150 and 280° C.

The heating step ii) is preferably carried out under an inert atmosphere, at atmospheric pressure. Indeed, one of the main advantages of the process in accordance with the invention is to not require a pressurized chamber due to the lack of volatility of the ionic liquid(s).

The heating may be carried out by various means, in particular by heating in an oven, or by microwave heating. It may be carried out continuously, in a heated chamber in which the ionic liquid and the precursors of the compound (I) flow, with a residence time that enables the reaction to be complete.

The duration of the heating step ii) generally varies from 10 minutes to 200 hours, preferably from 3 to 48 hours.

The separation of compound (I) during step iii) may be carried out by any technique known to a person skilled in the art such as, for example, by extraction with a solvent of the ionic liquid or by centrifugation, and removal of the possible by-products via an alcohol, a nitrile, a ketone or a chloroalkane having 1 to 6 carbon atoms.

At the end of the synthesis, the compound (I) may be washed, with an organic solvent such as, for example, acetone, acetonitrile or ethyl acetate, then used without further purification.

Likewise at the end of the synthesis, the ionic liquid may be recovered, optionally diluted by dichloromethane, chloroform, dichloroethane, methyl ethyl ketone, a pentanone, esters including ethyl acetate and ethyl formate, and washed, preferably with water and/or an acid solution such as, for example, an aqueous solution of hydrochloric acid, of sulfuric acid or sulfamic acid. After washing and drying (for example using Rotavapor®) or under primary vacuum, the ionic liquid may thus be used for a new synthesis, which is very advantageous from an economical viewpoint.

The process for preparing, a material (I) via a ceramic route uses the same precursors as the process by the ionothermal route. It consists in bringing powders of precursors into contact and in subjecting the mixture to a heat treatment. It is characterized in that:

-   -   the SO₄, Z and, where appropriate, Z′ elements are provided by a         single precursor in the form of a hydrated sulfate;     -   the F, A and, where appropriate A′ elements are each provided by         a fluoride;     -   the heat treatment is carried out in a sealed reactor.

The sulfate hydrate is preferably in (Z_(1−b)Z′_(b))SO₄.H₂O precursor monohydrate form.

The precursors are used in stoichiometric amounts, or with an excess of fluoride preferably of the order of 5 to 25%.

The mixture of powder is preferably pelleted via compression before being introduced into the reactor.

The heat treatment is carried out under temperature and pressure conditions that depend on the volume of the reactor (made of steel or made of quartz for example) and on the amount of precursors introduced into the reactor. The proportion of tavorite phase and of parasitic phases depends on the “mass of precursors treated/volume of the sealed reactor” ratio. It is noted that a higher confinement favors the production of a single tavorite phase. The determination of the conditions suitable for each particular case is within the scope of the person skilled in the art.

A material (I) according to the invention in which x=0, for example the compound FeSO₄F, may be obtained by electrochemical oxidation or by chemical oxidation of LiFeSO₄F in the presence of NO₂BF₄ or (CF₃CO₂)₂ICC₆H₅. It has a triclinic structure, space group P−1 with the following lattice parameters a=5.0683(7) (Å), b=5.0649(19) (Å), c=7.2552(19) (Å), α=69.36(3), β=68.80(3), γ=88.16(2), and V=161.52(8) (Å³).

A compound (I) may be used in various applications as a function of the elements that form it. By way of example, the compounds (I) of the invention may be used as active material for the manufacture of electrodes in batteries and electrochromic systems, as ceramics, as magnetic materials for storing information, as pigment, or in a photovoltaic cell as a light-absorbing material with a better result than that obtained with the aid of conventionally used TiO₂.

When a compound according to the invention is used as an electrode material, the electrode may be prepared by depositing onto a current collector a composite material obtained by mixing, via manual milling or via mechanical milling (for example via milling for around 10 minutes using an SPEX 1800 mill), a mixture comprising a compound of the invention and carbon. The percentage by weight of compound (I) relative to the “compound (I)+carbon” composite material may be from 50 to 99%, more particularly from 80 to 95%.

The composite material used for producing an electrode may also contain an additional compound, the compound (I)/additional compound weight ratio being greater than 5%. The additional compound may be, for example, a material with an olivine structure such as an LiMPO₄ material in which M represents at least one of the elements Fe, Co and Ni, or an oxide LiCoO₂ or LiNiO₂.

The amount of material deposited on the current collector is preferably such that the amount of compound according to the invention is between 0.1 and 200, preferably from 1 to 50 mg per cm². The current collector may consist of a grid or sheet of aluminum, of titanium, of graphite paper or of stainless steel.

An electrode according to the invention may be used in an electrochemical cell comprising a positive electrode and a negative electrode separated by an electrolyte. The electrode according to the invention forms the positive electrode.

The negative electrode may consist of metallic lithium or of one of its alloys, or of a transition metal oxide that forms, via reduction, a nanoscale dispersion in lithium oxide, or of a double nitride of lithium and of a transition metal. The negative electrode may also consist of a material capable of reversibly inserting Li⁺ ions at potentials of less than 1.6 V. As examples of such materials, mention may be made of low-potential oxides that have the general formula Li_(1+y+x/3)Ti_(2−x/3)O₄ (0≦x≦1, 0≦y≦1), Li_(4+x′)Ti₅O₁₂0≦x′≦3, carbon and carbon-based products resulting from the pyrolysis of organic materials, and also dicarboxylates.

The electrolyte advantageously comprises at least one lithium or sodium salt in solution in a polar aprotic liquid solvent, in a solvating polymer optionally plasticized by a liquid solvent or an ionic liquid, or in a gel consisting of a liquid solvent gelled by addition of a solvating or non-solvating polymer.

The present invention is illustrated by the following exemplary embodiments, to which it is not however limited.

Unless otherwise mentioned, FeSO₄.H₂O was prepared from FeSO₄.7H₂O by heating under vacuum at 200° C., or by heating FeSO₄.7H₂O in the EMI-TFSI ionic liquid at 250° C. for 2 hours.

EXAMPLE 1

In a preliminary step, FeSO₄.7H₂O was subjected to a heat treatment in EMI-TFSI at 250° C. for 10 h, then at 280° C. for 24 h. The FeSO₄.H₂O monohydrate formed is recovered by centrifugation, washed with ethyl acetate, then dried under vacuum at 100° C.

In a mortar, 0.85 g of FeSO₄.H₂O thus obtained and 0.148 g of LiF (1/1.14 molar ratio) were mixed, and the mixture was introduced into a Parr® bomb calorimeter and 5 ml of ethylmethylimidazolium bis(trifluoromethanesulfonyl)imide (EMI-TFSI) were added. The mixture was stirred for 20 min at room temperature, left to settle for 2 h, then heated at 300° C. for two hours, in the open bomb calorimeter, without stirring.

After cooling the reaction mixture to room temperature, the powder obtained was separated by centrifugation, washed 3 times with 20 ml of dichloromethane, then dried in an oven at 60° C.

The product obtained is in the form of a pale green-colored powder. It was subjected to various analyses.

SEM Analyses

FIG. 4 represents the image obtained by SEM and shows that the powder is in the form of agglomerates consisting of micron-sized particles.

TEM Analysis

FIG. 5 a represents the TEM image, more particularly the corresponding SAED diagram, and it shows that the particles consist of numerous crystallites. FIG. 5 b represents the EDS spectrum which shows the presence of F. The intensity is given on the y-axis (in arbitrary units) as a function of the energy E (in keV) on the x-axis.

X-Ray Diffraction

FIG. 6 represents the X-ray diffraction diagram and, in the form of an insert, the structure of the compound obtained. This structure comprises independent FeO₄F₂ octahedra (denoted by “2”), SO₄ tetrahedra (denoted by “1”) with tunnels in which the Li⁺ ions (denoted by “3”) are found,

Thermogravimetric Analysis (TGA)

FIG. 7 represents the diagram obtained during the characterization of the compound by TGA coupled with mass spectrometry. The upper curve (which is labeled with −1.14%, 0.07%, etc.) corresponds to the TGA analysis, the middle curve (which is labeled with 458.5° C. and 507.4° C.) corresponds to the differential scanning calorimetry (DSC) and the lower curve (labeled with m48 and m64) corresponds to the mass spectrometry. These curves show that a weight loss of 23.41% occurs between 400° C. and 700° C., corresponding to a departure of SO₂ which, under the electron impact in the mass spectrometers, partially fragments to SO. The irregularities in the TGA and DSC curve for is temperatures above 350° C. indicate the beginning of thermal instability of the compound.

The DSC and TGA analyses thus show that it is not possible to obtain LiFeSO₄F by a process via a ceramic route carried out at temperatures above 400° C. as described in US-2005/0163699.

To confirm this fact, a sample of the product obtained in the present example was heated in air for 30 minutes as in US-2005/0163699. FIG. 8 represents the change in the X-ray diffraction diagram during the increase in the temperature. RT denotes room temperature. The lines visible at 500° C. are attributed to the compounds that exist at this temperature, with reference to the numbers of the JCPDS files corresponding to the materials identified as follows:

* Fe₂O₃ (79-1741) | Fe₂O₃ (25-1402) Li₂SO₄ (32-064)+FeF₃.3H₂O (32-0464)  LiHSO₄ (31-0721) COMPARATIVE EXAMPLE 1

An equimolar mixture of anhydrous FeSO₄ and of LiF was prepared, and it was heated in air at 450° C. for 15 minutes.

FIG. 9 represents the X-ray diffraction diagram for the mixture of starting reactants (FIG. 9 a) and for the product obtained after the heat treatment at 450° C. for 15 min (FIG. 9 b). The peaks that correspondent respectively to FeSO₄ and to LiF are visible in FIG. 9 a, whereas FIG. 9 b shows peaks corresponding respectively to LiF, Li₂SO₄, Fe₂O₃ and Li₂S₂O₇.

This example confirms that the treatment, via a ceramic route, of a mixture of precursor of Fe and of S, and of a precursor of F does not give the compound LiFeSO₄F under the conditions described in US-2005/0163699.

EXAMPLE 2 Synthesis of LiFeSO₄F from FeSO₄.7H₂O and LiF in EMI-TFSI

Introduced into a PTFE flask containing 3 ml of 1-ethyl-3-methylimidazolium bis(trifluoromethanesulfonyl)imide (EMI-TFSI) was a mixture of 1.404 g of FeSO₄.7H₂O and 0.149 g of LiF prepared in a mortar, the mixture was subjected to magnetic stirring for 20 minutes at room temperature, the stirring was stopped, then 2 ml of ionic liquid (EMI-TFSI) were added, and the mixture was kept without stirring at room temperature for 30 minutes. The whole assembly was then introduced into an oven at 200° C., the temperature of the oven was increased, by 10° C. every 20 minutes up to 275° C., kept at this value for 12 hours, then left to cool slowly.

The powder that was formed during the heat treatment was separated from the ionic liquid by centrifugation, washed 3 times with 10 ml of dichloromethane, then dried in an oven at 60° C.

The refinement of the X-ray diffraction spectrum carried out with a copper cathode (represented in FIG. 10) shows the presence of two phases, LiFeSO₄F and FeSO₄.H₂O, in equivalent proportions.

Phase 1: LiFeSO₄F

Triclinic, space group: P−1 (2) A=5.1819(5) Å, b=5.4853(4) Å, c=7.2297(4) Å, α=106.4564(3)°, β=107.134(6)°, γ97.922(5)°

V=182.761(4) Å³. Phase 2: FeSO₄.H₂O

Triclinic, space group: P−1 (2) A=5.178(7) Å, b=5.176(7) Å, c=7.599(7) Å; α=107.58(6)°, β=107.58(8)°, γ=93.34(6)°

V=182.56(4) Å³. EXAMPLE 3 Synthesis of LiFeSO₄F from FeSO₄.7H₂O and LiF in EMI-TFSI

Introduced into a PTFE flask containing 3 ml of 1-ethyl-3-methylimidazolium bis(trifluoromethanesulfonyl)imide (EMI-TFSI) was a mixture of 0.85 g of FeSO₄.H₂O and 0.149 g of LiF (1/1.14 molar ratio) prepared in a mortar, the mixture was subjected to magnetic stirring for 20 minutes at room temperature, the stirring was stopped, then 2 ml of ionic liquid (EMI-TFSI) were added, and the mixture was kept without stirring at room temperature for 30 minutes. The whole assembly was then introduced into an oven at 200° C., the temperature of the oven was increased by 10° C. every 20 minutes up to 275° C., kept at this value for 12 hours, then left to cool slowly.

The powder that was formed during the heat treatment was separated from the ionic liquid by centrifugation, washed 3 times with 10 ml of dichloromethane, then dried in an oven at 60° C.

The refinement of the X-ray diffraction spectrum carried out with a copper cathode (represented in FIG. 11) shows the presence of a single, LiFeSO₄F phase, the lattice parameters of which are as follows:

Triclinic, space group: P−1 (2) a=5.1827(7) Å, b=5.4916(6) Å, c=7.2285(7) Å, α=106.535(7)°, β=107.187(6)°, γ97.876(5)°

V=182.95(4) Å³.

The comparison of examples 2 and 3 shows that the use of a sulfate monohydrate is more favorable than the use of a sulfate heptahydrate, insofar as the first mentioned makes it possible to obtain a single phase, whereas the second gives a mixture.

EXAMPLE 4 Synthesis of LiFeSO₄F from FeSO₄.H₂O and LiF

The synthesis of LiFeSO₄F is carried out via an ionothermal route in an autoclave at 280° C.

Introduced into an autoclave containing 3 ml of 1-ethyl-3-methylimidazolium bis(trifluoromethanesulfonyl)imide (EMI-TFSI) was a mixture of 0.85 g of FeSO₄.H₂O and 0.149 g of LiF (1/1.14 molar ratio) prepared in a mortar, the mixture was subjected to magnetic stirring for 30 minutes at room temperature, the stirring was stopped, then 2 ml of ionic liquid (EMI-TFSI) were added, and the mixture was kept without stirring at room temperature for 30 minutes. After sealing the autoclave under argon, the whole assembly was then introduced into an oven at 200° C., the temperature of the oven was increased by 10° C. every 20 minutes up to 280° C. kept at this value for 48 hours, then left to cool slowly.

The powder that was formed during the heat treatment was separated from the ionic liquid by centrifugation, washed 3 times with 10 ml of dichloromethane, then dried in an oven at 60° C.

The product obtained is in the form of a whitish powder. The slightly different color from that of the sample from example 1 denotes an aptitude for the non-stoichiometry of the phases, according to the operating conditions.

The refinement of the X-ray diffraction spectrum carried out with a copper cathode (represented in FIG. 12) shows the presence of a single, LiFeSO₄F phase, the lattice parameters of which are as follows:

Triclinic, space group: P−1 (2) a=5.1782(4) Å, b=5.4972(4) Å, c=7.2252(4) Å, α=106.537(4)°, β=107.221(4)°, γ=97.788(3)°

V=182.82(4) Å³. EXAMPLE 5 Synthesis of LiFeSO₄F from FeSO₄.H₂O and LiF in 1-butyl-3-methylimidazolium trifluoromethanesulfonate (triflate)

The synthesis of LiFeSO₄F is carried out via an ionothermal route in an autoclave at 270° C.

Introduced into an autoclave containing 3 ml of 1-butyl-3-methylimidazolium trifluoromethanesulfonate (triflate) was a mixture of 0.85 g of FeSO₄.H₂O and 0.149 g of LiF (1/1.14 molar ratio) prepared in a mortar, the mixture was subjected to magnetic stirring for 30 minutes at room temperature, the stirring was stopped, then 2 ml of ionic liquid (EMI-Tf) were added, and the mixture was kept without stirring at room temperature for 30 minutes. After sealing the autoclave under argon, the whole assembly was then introduced into an oven at 200° C., the temperature of the oven was increased, by 10° C. every 20 minutes up to 270° C., kept at this value for 48 hours, then left to cool slowly.

The powder that was formed during the heat treatment was separated from the ionic liquid by centrifugation, washed 3 times with 10 ml of dichloromethane, then dried in an oven at 60° C.

The refinement of the X-ray diffraction spectrum carried out with a cobalt cathode (represented in FIG. 13) shows the presence of an LiFeSO₄F phase (representing around 50% by weight), and two “anhydrous FeSO₄” phases.

Phase 1: LiFeSO₄F, Triclinic, space group P−1 (2) Phase 2: orthorhombic, space group Cmcm (63) Phase 3: orthorhombic, space group Pbnm (62)

The comparison of examples 4 and 5 shows that the use of a hydrophobic ionic liquid is more favorable than the use of a hydrophilic ionic liquid, insofar as the first mentioned makes it possible to obtain a single phase, whereas the second gives a mixture.

EXAMPLE 6 Synthesis of LiCoSO₄F from CoSO₄.H₂O and LiF in EMI-TFSI

The CoSO₄.H₂O precursor used was prepared from CoSO₄.H₂O by heating under vacuum at 160° C. for 2 hours.

Introduced into a PTFE flask containing 5 ml of 1-ethyl-3-methylimidazolium bis(trifluoromethanesulfonyl)imide (EMI-TFSI) was a mixture of 0.86 g of CoSO₄.H₂O and 0.149 g of LiF (1/1.13 molar ratio) prepared in a mortar, the mixture was subjected to magnetic stirring for 20 minutes at room temperature and the stirring was stopped. The flask was then sealed under argon, and the reaction mixture was kept without stirring at room temperature for 30 minutes. The whole assembly was then introduced into an oven at 250° C., the temperature of the oven was increased by 5° C. every 10 minutes up to 275° C., kept at this value for 36 hours, then left to cool slowly.

The powder that was formed during the heat treatment was separated from the ionic liquid by centrifugation, washed 3 times with 10 ml of ethyl acetate, then dried in an oven at 60° C.

The refinement of the X-ray diffraction spectrum carried out with a cobalt cathode (represented in FIG. 14) shows the presence of a single, LiCoSO₄F phase, the lattice parameters of which are as follows:

a=5.1719(6) Å, b=5.4192(6) Å, c=7.1818(7) Å, α=106.811(7)°, β=107.771(7)°, γ=97.975 (5)°

V=177.71(3) Å³.

The curve obtained by thermogravimetric analysis is represented in FIG. 15. It shows a loss of weight starting from 400° C., prove that the compound LiCoSO₄F is decomposed. It cannot therefore be obtained by a process in the solid phase using higher temperatures.

To confirm this fact, a sample of the product obtained in the present example was heated in air for 30 minutes as in US-2005/0163699. FIG. 16 represents the change in the X-ray diffraction diagram during the increase in the temperature. RT denotes room temperature. The arrows denote the zones in which the peaks corresponding to decomposition products are found. It thus appears that the compound begins to decompose at 375° C. The label “RT” given on the right of the lower curve signifies “room temperature”.

EXAMPLE 7 Synthesis of LiNiSO₄F from NiSO₄.H₂O and LiF in EMI-TFSI

The NiSO₄.H₂O monohydrate used as precursor was prepared from NiSO₄.7H₂O by heating under vacuum at 240° C. for 2 hours.

Introduced into a PTFE flask containing 5 ml of 1-ethyl-3-methylimidazolium bis(trifluoromethanesulfonyl)imide (EMI-TFSI) was a mixture of 0.86 g of NiSO₄.H₂O and 0.149 g of LiF (1/1.13 molar ratio) prepared in a mortar, the mixture was subjected to magnetic stirring for 20 minutes at room temperature and the stirring was stopped. The flask was then sealed under argon, and the reaction mixture was kept without stirring at room temperature for 30 minutes. The whole assembly was then introduced into an oven at 250° C., the temperature of the oven was increased up to 285° C. over 2 hours, kept at this value for 36 hours, then left to cool slowly.

The powder that was formed during the heat treatment was separated from the ionic liquid by centrifugation, washed 3 times with 10 ml of ethyl acetate, then dried in an oven at 60° C.

The X-ray diffraction diagram produced with a cobalt cathode (represented in FIG. 17) shows that the compound obtained contains more than 90.95% of a phase similar to that of LiFeSO₄F or LiCoSO₄F. The lattice parameters of this phase are as follows:

Triclinic, space group: P−1 (2) a=5.173(1) Å, b=5.4209(5) Å, c=7.183(1) Å, α=106.828(9)°, β=107.776(8)°, γ=97.923 (8)°

V=177.85(5) Å³.

The curve obtained by thermogravimetric analysis is represented in FIG. 18. It shows a loss of weight starting from 380° C., proof that the compound LiNiSO₄F is decomposed. It cannot therefore be obtained by a process in the solid phase using higher temperatures.

To confirm this fact, a sample of the product obtained in the present example was heated in air for 30 minutes as in US-2005/0163699. FIG. 19 represents the change in the X-ray diffraction diagram during the increase in the temperature. The arrows denote the zones in which the peaks corresponding to decomposition products are found. It thus appears that the compound begins to decompose at 375° C. The label “RT” given on the right of the lower curve signifies “room temperature”.

EXAMPLE 8 LiFe_(1−y)Mn_(y)SO₄F Solid Solution

An LiFe_(1−y)Mn_(y)SO₄F compound was prepared from LiF and from a Fe_(1−y)Mn_(y)SO₄.H₂O solid solution as precursor.

Preparation of the Precursor

1-y mol of FeSO₄.7H₂O and y mol of MnSO₄.H₂O were dissolved in 2 ml of water previously degassed under argon to prevent the oxidation of Fe(II), then 20 ml of ethanol was added. The powder which formed by precipitation during the addition of ethanol was recovered by centrifugation, washed twice with 20 ml of ethanol, then heated at 200° C. under vacuum for 1 hour.

Several samples were prepared, varying the value of y.

The samples were analyzed by X-ray diffraction. The diffraction diagram of the “y=0.5” sample obtained, is represented in FIG. 20. It shows that it is the Fe_(0.5)Mn_(0.5)SO₄.H₂O solid solution, the lattice parameters of which are as follows:

Triclinic, space group: P−1 (2) a=5.2069 Å, b=5.2056 Å, c=7.6725 Å, α=107.7196°, β=107.4498°, γ=93.08°

V=186.56 Å³.

Preparation of the LiFe_(1−y)Mn_(y)SO₄F Solid Solution

The synthesis is carried out via an ionothermal route in an autoclave at 270° C., for various precursor samples.

Introduced into an autoclave containing 3 ml of 1-ethyl-3-methylimidazolium bis(trifluoromethanesulfonyl)imide (EMI-TFSI) was a mixture of 0.85 g of Fe_(0.5)Mn_(0.5)SO₄.H₂O and 0.149 g of LiF (1/1.14 molar ratio) prepared in a mortar, the mixture was subjected to magnetic stirring for 20 minutes at room temperature, the stirring was stopped, then 2 ml of ionic liquid (EMI-TFSI) were added, and the mixture was kept without stirring at room temperature for 30 minutes. After sealing the autoclave under argon, the whole assembly was then introduced into an oven at 200° C., the temperature of the oven was increased by 10° C. every 20 minutes up to 270° C., and kept at this value for 48 hours, then left to cool slowly.

The powder that was formed during the heat treatment was separated from the ionic liquid by centrifugation, washed 3 times with 10 ml of dichloromethane, then dried in an oven at 60° C.

The X-ray diffraction shows the formation of LiFe_(1−y)Mn_(y)SO₄F solid solution at low values of y (in particular for y<0.1) and the formation of mixed phases for the higher values of y (in particular for y>0.25).

EXAMPLE 9 Synthesis of NaFeSO₄F from FeSO₄.7H₂O and NaF

A mixture of 5 ml of EMI-TFSI and 2.808 g of FeSO₄.7H₂O was introduced into an open Parr® bomb calorimeter, and heated at 230° C. After heating for 5 h, the mixture was cooled to room temperature, then 0.42 g of NaF was added before sealing the Parr® bomb calorimeter. After 10 minutes of magnetic stirring, the mixture was heated at 250° C. for 24 hours. After cooling to room temperature, the powder recovered was washed twice with 20 ml of acetone, then dried in an oven at 60° C. The X-ray diffraction diagram, represented in FIG. 21, shows the formation of a new phase having a monoclinic distorted tavorite-type structure having the space group P2_(1/C).

In the examples, FeO₄.H₂O and CoSO₄.H₂O were prepared by heating FeSO₄.7H₂O and CoSO₄.7H₂O respectively and applying primary vacuum at 200° C. for 1 hour.

EXAMPLE 10 Synthesis of LiFeSO₄F

In a mortar, 0.850 g of FeSO₄.H₂O monohydrate was mixed manually with 0.145 g of LiF, which corresponds to a 10% excess of LiF relative to the stoichiometric amounts. The powder was pelleted under a 10 tonne load, then the pellet was introduced into a Parr bomb calorimeter that was assembled in a dry box using argon as the carrier gas. The bomb calorimeter was then placed in an oven, the temperature of which was brought to 280° C. over 5 hours and maintained at this value for 60 hours. The oven was then rapidly cooled, the pellet was recovered and milled in order to characterize it via XRD.

The XRD diagram is represented in FIG. 22. It shows that the product obtained is a 95% single-phase product.

EXAMPLE 11 Synthesis of LiFeSO₄F from FeSO₄.H₂O and LiF at 280° C. (Effect of the Internal Pressure)

A mixture of FeSO₄.H₂O/LiF powders in a 1/1.14 molar ratio was prepared, and a pellet was prepared by compressing 1 g of powder mixture under a 10 tonne load. The pellet was introduced into a Parr bomb calorimeter that was assembled in a dry box using argon as the carrier gas. The Parr bomb calorimeter was then subjected to a heat treatment according to the following scheme: 1 h at 250° C., 1 h at 260° C., 1 h at 270° C., 60 h at 280° C., slow cooling. The oven was then rapidly cooled, the pellet was recovered and it was milled in order to characterize it by XRD (CuKα).

This procedure was carried out, on the one hand, in a Parr bomb calorimeter of 25 ml and, on the other hand, in a Parr bomb calorimeter of 50 ml.

The XRD diagrams are represented in FIG. 23. The upper curve corresponds to the implementation in the 25 ml Parr bomb calorimeter and the lower curve corresponds to the implementation in the 50 ml Parr bomb calorimeter. The diagrams show that the formation of the LiFeSO₄F phase characteristic of the lines identified by the sign * and of impurities. The level of impurities is lowest in the 25 ml bomb calorimeter, namely around 5%.

EXAMPLE 12 Synthesis of LiFeSO₄F Starting from FeSO₄.H₂O and LiF at 290° C.

A mixture of 0.850 g of FeSO₄H₂O and 0.2 g of LiF was prepared by mechanical milling for 10 min in an SPEX-800 mill, then the mixture was pelleted under a 10 tonne load and the pellet obtained was placed in a 25 ml Parr bomb calorimeter that was sealed under argon. The following heat treatment was then applied: 1 h at 250° C., 1 h at 260° C., 1 h at 270° C., 48 h at 290° C., slow cooling. The oven was then rapidly cooled, the pellet was recovered and it was milled in order to characterize it by XRD (CuKα). FIG. 24 represents the XR diffraction diagram (left-hand section) and a scanning electron microscopy photo (right-hand section). The XRD diagram shows the formation of a pure LiFeSO₄F phase, crystallized in a triclinic lattice, of space group P⁻¹, with the following lattice parameters: a=5.1865(11) (Å), b=5.4863(9) (Å), c=7.2326(12) (Å), α=106.49(1), β=107.153(9), γ=97.888 (8), and a volume V=182.99(6) Å³. The scanning electron microscopy photo shows agglomerates of small nanoscale particles that are very varied in size (400 nm to 800 nm).

EXAMPLE 13 Synthesis of NaFeSO₄F

In a mortar, 0.850 mg of FeSO₄.H₂O monohydrate was mixed manually with 24545 mg of NaF, which corresponds to a 10% excess of NaF relative to the stoichiometric amounts. The powder was pelleted under a pressure of 10 000 psi, then the pellet was introduced into a Parr bomb calorimeter that was assembled in a dry box using argon as the carrier gas. The bomb calorimeter was then placed in an oven, the temperature of which was brought to 290° C. over 5 hours and maintained at this value for 80 hours. The oven was then rapidly cooled, the pellet was recovered and milled in order to characterize it via XRD. The XRD diagram is represented in FIG. 25. It shows that the compound obtained is NaFeSO₄F and crystallizes into a monoclinic lattice (space group P2₁/c) with the following parameters: a=6.6798(2) (Å), b=8.7061(2) (Å), c=7.19124(18) (Å), b=113.517(2) (Å) and V=383.473 (Å³).

EXAMPLE 14 Synthesis of NaCoSO₄F

In a mortar, 0.855 mg of CoSO₄.H₂O monohydrate was mixed manually with 245 ma of NaF, which corresponds to a 10% excess of NaF relative to the stoichiometric amounts. The powder was pelleted under a pressure of 10 000 psi, then the pellet was introduced into a Parr bomb calorimeter that was assembled in a thy box using argon as the carrier gas. The bomb calorimeter was then placed in an oven, the temperature of which was brought to 300° C. over 5 hours and maintained at this value for 1 week. The oven was then rapidly cooled, the pellet was recovered and milled in order to characterize it via XRD. The XRD diagram is represented in FIG. 26. It shows the predominant presence of the NCoSO₄F phase which crystallizes in the space group P2₁/c with the lattice parameters a=6.645(2) Å, b=8.825(2) Å, c=7.162(2) Å, β=112.73(3) and V=387.38(3) Å³.

EXAMPLE 15 Preparation of FeSO₄F

The compound was prepared by chemical delithiation of LiFeSO₄F with NO₂OF₄ in acetonitrile at room temperature. The X-ray diffraction spectrum represented in FIG. 27 shows that the compound crystallizes into a lattice, the parameters of which are:

Triclinic, space group: P−1 (2) A=5.0682 Å, b=5.0649 Å, c=7.255 Å α=69.36°, β=68.80°, γ=88.16°

V=161.52 Å³. EXAMPLE 18 Electrochemical Tests

Samples of compound LiFeSO₄F, prepared according to example 3, were tested as a positive electrode material in a Swagelok cell in which the electrode is a lithium foil, the two electrodes being separated by a polypropylene separator soaked by a 1M solution of LiPF₆ in a 1/1 ethylene carbonate/dimethyl carbonate EC-DMC mixture. To produce a positive electrode, 80 mg of LiFeSO₄F (in the form of particles having a mean diameter of 1 μm) and 20 mg of carbon were mixed by mechanical milling in an SPEX 1800 mill for 15 minutes. An amount of mixture corresponding to 8 mg of LiFeSO₄F per cm² was applied to an aluminum current collector.

In FIG. 28 a, the main curve represents the variation of the potential as a function of the insertion rate of lithium, during the cycling of the cell at a C/10 regime, and the insert represents the change in the capacity of a cell during the succession of cycles at a C/10 regime, N being the number of cycles.

FIG. 28 b represents the variation of the potential as a function of the insertion rate of lithium, during the cycling of the cell at a C/2 regime.

FIG. 28 c represents the variation of the capacity of a cell as a function of the cycling regime R.

It thus appears that the capacity remains at 90% at a C/2 regime and at 67% at a C/10 regime.

EXAMPLE 19 Electrochemical Test

An LiFeSO₄F sample prepared according to example 12 was subjected to an electrochemical test. An LiFeSO₄F (ceramic)/carbon (acetylene black) composite material in an 85/15 weight proportion was prepared by mechanical milling for 15 min in an SPEX® mill. This composite material was applied to an aluminum current collector and it was mounted in a cell in which the negative anode is a lithium foil and the electrolyte is a commercial electrolyte of LP30 type. The cell thus obtained was cycled in the potential window [2.5 V-4.5 V] under a C/5 regime (1 electron exchanged over 5 hours). The results of the electrochemical tests are represented in FIG. 29, in which the left-hand curve represents the variation of the potential as a function of the lithium ion content in the fluorosulfate, and the right-hand curve represents the variation of the capacity as a function of the number of cycles. It appears that the material electrochemical activity is centered in the vicinity of 3.6 V, with a reversible capacity of around 80 mAh/g which is stable at least in the first 5 cycles.

EXAMPLE 20 Electrochemical Test

An NaFeSO₄F sample prepared according to example 13 was tested under the conditions of example 19. The cycling curve is represented in FIG. 30. It shows that the material has an electrochemical activity similar to that of the corresponding material prepared in an ionic liquid medium. In particular, the phase the reactivity with respect to Li is limited to 0.2 Li per formula unit, irrespective of the preparation process. 

1. A material consisting of particles of a fluorinated compound which has a distorted tavorite-type structure and which corresponds to the following formula (I): (A_(1−a)A′_(a))_(x)(Z_(1−b)Z′_(b))_(z)(SO₄)_(s)F_(f)  (I) in which A represents Li or Na; A′ represents a vacancy or at least one dopant element; Z represents at least one element chosen from Fe, Co and Ni; Z′ represents a vacancy or at least one dopant element; the indices a, b, x, z, s, and f are chosen so as to ensure the electroneutrality of the compound, and a≧0, b≧0, x≧0, z>0, s>0, f>0; the respective amounts a and b of dopant A and Z′ are such that the tavorite-type structure is preserved.
 2. The material as claimed in claim 1, wherein a≧0.25 and b≧0.25.
 3. The material as claimed in claim 1, wherein A is Li and the distorted tavorite-type structure of compound (I) has a triclinic lattice of space group P−1 or A is Na and the distorted tavorite-type structure of compound (I) has a monoclinic lattice.
 4. The material as claimed in claim 1, wherein said material is in the form of grains, the dimension of which is less than 100 μm.
 5. The material as claimed in claim 1, wherein A′ is an alkali metal different from A, an alkaline-earth metal or a 3d metal.
 6. The material as claimed in claim 1, wherein Z′ is a metal chosen from alkali metals, Mn, Mg, Ca, Sc, Ti, V, Cr, Zn, Al, Ga, Sn, Zr, Nb and Ta in at least one of their degrees of oxidation.
 7. The material as claimed in claim 1, wherein the fluorinated compound corresponds to one of the formulae Li(Z_(1−b)Z′_(b))SO₄F and Na(Z_(1−b)Z′_(b))_(z)SO₄F.
 8. A process for preparing a material as claimed in claim 1, wherein said method comprises the steps of: i) dispersing said precursors in a support liquid comprising at least one ionic liquid consisting of a cation and of an anion, the electric charges of which are balanced, in order to obtain a suspension of said precursors in said liquid; ii) heating said suspension to a temperature of 25 to 330° C.; iii) separating said ionic liquid and the inorganic oxide of formula (I) resulting from the reaction between said precursors.
 9. The process as claimed in claim 9, wherein the amount of precursors present within the ionic liquid during step i) is from 0.01% to 85% by weight.
 10. A process for preparing a material as claimed in claim 1, which consists in bringing powders of precursors into contact and in subjecting the mixture to a heat treatment, wherein: the SO₄, Z and, where appropriate, Z′ elements are provided by a single precursor in the form of a hydrated sulfate; the F, A and, where appropriate, A′ elements are each provided by a fluoride; the heat treatment is carried out in a sealed reactor.
 11. The process as claimed in claim 11, wherein the mixture of powder is pelleted via compression before being introduced into the reactor.
 12. The process as claimed in claim 9, wherein the precursor of Li is chosen from inorganic acid salts, volatile organic acid salts, heat-decomposable acid salts, fluorides and sulfates.
 13. The process as claimed in claim 9, wherein the precursor of a Z or Z′ element is chosen from the sulfates and/or the phosphates of Z that have a tavorite-type structure.
 14. The process as claimed in claim 9, wherein the precursor of Z and, where appropriate, of Z′ is a monohydrate ZSO₄.H₂O or Z′SO₄.H₂O or a mixed monohydrate Z_(1−b)Z′_(b)SO₄.H₂O, and the precursor of A and, where appropriate, of A′ is a fluoride.
 15. An electrode comprising an active material on a current collector, wherein the active material is a material as claimed in claim
 1. 16. An electrochemical cell comprising a positive electrode and a negative electrode separated by an electrolyte, wherein the positive electrode is an electrode as claimed in claim
 15. 17. The material as claimed in claim 1, wherein the fluorinated compound corresponds to the formula (Z_(1−b)Z′_(b))_(z)(SO₄)_(s)F_(f), 